Non-aqueous electrolyte secondary battery

ABSTRACT

A non-aqueous electrolyte secondary battery having an improved negative electrode is disclosed. The negative electrode comprises alloy particles having a composition represented by the formula: 
     
       
         Li x M 1   a M 2   (1) 
       
     
     wherein M 1  represents at least one element selected from the element group m 1  consisting of Ti, Zr, V, Sr, Ba, Y, La, Cr, Mo, W, Mn, Co, Ir, Ni, Cu and Fe, M 2  represents at least one element selected from the element group m 2  consisting of Mg, Ca, Al, In, Si, Sn, Pb, Sb and Bi, M 1  and M 2  represent different elements each other, and wherein 0≦x≦10, 0.1≦a≦10, with the proviso that 2≦a≦10 when M 1  is composed only of Fe, and having at least two phases which are different in composition each other.

This Application is a continuation of PCT/JP99/05805 filed Oct. 20, 1999.

TECHNICAL FIELD

The present invention relates to a non-aqueous electrolyte secondary battery, particularly an improvement of a negative electrode which reversibly absorbs and desorbs lithium.

BACKGROUND ART

There have been various vigorous studies on a non-aqueous electrolyte secondary battery including lithium or a lithium compound as the negative electrode, because it is to be expected to offer a high voltage as well as a high energy.

To date, oxides and chalcogens of transition metals like LiMn₂O₄, LiCoO₂, LiNiO₂, V₂O₅, Cr₂O₅, MnO₂, TiS₂, MoS₂ and the like are known positive electrode active materials for non-aqueous electrolyte secondary batteries. Those compounds have a layered or tunneled structure that allows free intercalation and deintercalation of lithium ions. On the other hand, there are many previous studies on metallic lithium as the negative electrode active material. However, metallic lithium has a drawback that a deposition of lithium dendrites occurs on the surface of the electrode during charging, which reduces charge/discharge efficiency or causes internal short-circuiting due to contact between formed lithium dendrites and the positive electrode. As one measure for solving such drawback, the use of a lithium alloy such as lithium-aluminum alloy which not only suppresses the growth of lithium dendrites but also can absorb therein and desorb therefrom lithium as the negative electrode has been under investigation. However, the use of such lithium alloy has a drawback that repeated charge/discharge operation causes pulverization of the electrode, which in turn deteriorates the cycle life characteristics. At present, lithium ion batteries have been put into practical use that include as the negative electrode a graphite-based carbon material having excellent cycle life characteristics and safety capable of reversibly absorbing and desorbing lithium although smaller in capacity than the above-mentioned negative electrode active materials.

When the above-mentioned graphite material is used in a negative electrode, the practical capacity used thereof is 350 mAh/g which is a value near the theoretical capacity (372 mAh/g). Since the theoretical density is as low as 2.2 g/cc and the density further decreases when the graphite material is formed into a negative electrode sheet, use of metallic materials having higher capacity per volume as the negative electrode is desired.

However, problems arising when metallic materials are used as the negative electrode include pulverization caused by repeated expansion and contraction accompanying intercalation and deintercalation of lithium. Due to this pulverization, the reactivity of the active material lowers and charge/discharge cycle life shortens.

For solving these problems, there has been for example a suggestion for solving pulverization, intending to suppress expansion by means of stress relaxation of a phase not absorbing lithium even under charged condition (absorbing condition) in coexistence in one particle of a phase absorbing lithium and a phase not absorbing lithium (Japanese Laid-Open Patent Publication (JP-A) No. 11-86854). Further, there has been a suggestion in which two or more phases absorbing lithium are allowed to exist in one particle, intending to relax expansion due to change in structure during absorbing lithium of each phase for suppression of pulverization (JP-A No. 11-86853).

However, even a negative electrode material produced by utilizing these means causes pulverization of the active material along with progress of a charge/discharge cycle, thereby to increase cycle deterioration. The reason for this is hypothesized as follows. Namely, when a plurality of phases are present in an active material particle, even if releasing of expansion stress into the interface of phases is possible, non-uniformity in stress tends to occur in an active material particle along with increase in expansion coefficient of each phase. Therefore, pulverization occurs from some phases on which expansion stress is applied significantly, and this pulverized material liberates from the active material particle. Thus, pulverization of the active material progresses. When one phase is composed solely of an element easily forming an alloy with lithium, the pulverization as described above tends to occur more easily.

The object of the present invention is to provide a negative electrode for non-aqueous electrolyte secondary batteries having high electric capacity and excellent charge/discharge cycle life characteristics, in view of the above-described drawbacks.

The present invention provides a negative electrode for non-aqueous electrolyte secondary batteries satisfying high electric capacity and long cycle life at the same time by preventing pulverization accompanying expansion and contraction.

DISCLOSURE OF INVENTION

The non-aqueous electrolyte secondary battery of the present invention comprises a rechargeable positive electrode, a rechargeable negative electrode and a non-aqueous electrolyte, and the negative electrode comprises alloy particles having a composition represented by the formula:

Li_(x)M¹ _(a)M²  (1)

wherein M¹ represents at least one element selected from the element group m¹ consisting of Ti, Zr, V, Sr, Ba, Y, La, Cr, Mo, W, Mn, Co, Ir, Ni, Cu and Fe, M² represents at least one element selected from the element group m² consisting of Mg, Ca, Al, In, Si, Sn, Pb, Sb and Bi, M¹ and M² represent different elements each other, and wherein 0≦x≦10, 0.1≦a≦10, with the proviso that 2≦a≦10 when M¹ is composed only of Fe, and at least two phases having different compositions are present in the afore-mentioned alloy.

It is preferable that the afore-mentioned at least two phases have compositions represented by the formula (2) and the formula (3), respectively:

M³ _(c)M⁴  (2)

M⁵ _(d)M⁶  (3)

wherein each of M³ and M⁵ represents at least one element selected from the element group m¹, each of M⁴ and M⁶ represents at least one element selected from the element group m², and wherein 0.25≦c<3, 1≦d≦10 and c<d.

Herein, M¹ preferably represents at least one element selected from the group consisting of Ti, Zr, Mn, Co, Ni, Cu and Fe. M¹ represents most preferably at least one element selected from the group consisting of Ti, Cu and Fe which are elements having lowest electrochemical reactivity with lithium, among them. M² preferably represents at least one element selected from the group consisting of Al, Si and Sn. M² represents most preferably at least one element selected from the group consisting of Si and Sn which are elements having highest electrochemical reactivity with lithium, among them.

BRIEF DESCRIPTION OF DRAWINGS

FIG. 1 is a schematic longitudinal section of a test cell for evaluating electrode characteristics of a negative electrode material of the present invention.

FIG. 2 is a schematic longitudinal section of a cylindrical battery for evaluating characteristics of a battery equipped with a negative electrode of the present invention.

BEST MODE FOR CARRYING OUT THE INVENTION

The negative electrode of the present invention comprises alloy particles having a composition represented by the formula:

Li_(x)M¹ _(a)M²  (1)

wherein M¹ represents at least one element selected from the element group m¹ consisting of Ti, Zr, V, Sr, Ba, Y, La, Cr, Mo, W, Mn, Co, Ir, Ni, Cu and Fe, M² represents at least one element selected from the element group m² consisting of Mg, Ca, Al, In, Si, Sn, Pb, Sb and Bi, M¹ and M² represent different elements each other, and wherein 0≦x≦10, 0.1≦a≦10, with the proviso that 2≦a≦10 when M¹ is composed only of Fe, and having at least two phases different in composition each other.

The above-mentioned at least two phases preferably have compositions represented by the formula (2) and the formula (3), respectively:

M³ _(c)M⁴  (2)

M⁵ _(d)M⁶  (3)

wherein each of M³ and M⁵ represents at least one element selected from the element group m¹, each of M⁴ and M⁶ represents at least one element selected from the element group m², and wherein 0.25≦c≦3, 1≦d≦10 and c<d.

In the alloy particle constituting the negative electrode of the present invention, pulverization is suppressed by combination of a phase having a composition represented by the above-mentioned formula (2) (hereinafter referred to Phase A) with a phase having a composition represented by the above-mentioned formula (3) (hereinafter referred to Phase B), and as a result, deterioration due to charge/discharge cycles is suppressed. Phase A has a higher proportion of the element selected from the element group m², as compared with Phase B. The elements selected from the element group m² are metallic elements which tend to electrochemically react with lithium to form a uniform alloy, and higher ratio thereof indicates that the phase reacts with lithium in significant amount. Therefore, Phase A can absorb lithium in larger amount as compared with Phase B. Therefore, Phase A reveals larger expansion during charging. By coexistence of Phase B absorbing a smaller amount of lithium but showing also smaller expansion during charging with Phase A, the difference in expansion stresses of both phases can be decreased and cracking of the whole alloy particle can be prevented. On the other hand, when a phase inactive with lithium is combined with Phase A, only Phase A expands, and as a result, the difference in expansion stresses of both phases is large, and the particle tends to be cracked. By combination of Phase A with an inactive phase, the electric capacity decreases.

In the alloy particle of the present invention, the difference between expansion stresses of combined Phase A and Phase B is small so that expansion of the whole alloy particle is relaxed to give suppressed pulverization as compared with conventional examples, as described above. It is desirable that both of Phase A and Phase B in one particle are constituted of a plurality of crystal grains.

Preferable combination examples of Phase A with Phase B in the present invention will be listed below.

(a) Phase A is composed of one or more of SrSn₃, BaSn₃, LaSn₂, ZrSn₂, MnSn₂, CoSn₂ or FeSn₂, and Phase B is composed of one or more of La₂Sn, Zr₃Sn₂, Zr₄Sn, V₃Sn, MnSn, Mn₂Sn, Mn₃Sn, FeSn, Fe_(1.3)Sn, Fe₃Sn, CoSn, Co₃Sn₂, Ni₃Sn₂, Ni₃Sn, Cu₆Sn₅, Cu₃Sn, Cu₄Sn, Ti₆Sn₅ or Ti₂Sn.

(b) Phase A is composed of one or two of FeSn or CoSn, and Phase B is composed of one or more of La₂Sn, Zr₃Sn₂, Zr₄Sn, V₃Sn, Mn₂Sn, Mn₃Sn, Fe_(1.3)Sn, Fe₃Sn, Co₃Sn₂, Ni₃Sn₂, Ni₃Sn, Cu₆Sn₅, Cu₃Sn, Cu₄Sn, Ti₆Sn₅ or Ti₂Sn.

(c) Phase A is composed of one or two of Ti₆Sn₅ or Cu₆Sn₅, and Phase B is composed of one or more of La₂Sn, Zr₃Sn₂, Zr₄Sn, V₃Sn, Mn₂Sn, Mn₃Sn, Ti₃Sn, Cu₃Sn, Fe₃Sn, Fe₆Sn, Fe₁₂Sn, Co₃Sn₂, Ni₃Sn₂, Ni₃Sn, Cu₄Sn or Ti₂Sn.

(d) Phase A is composed of one or more of SrSn, Ba₂Sn, La₂Sn or Ti₂Sn, and Phase B is composed of one or more of Mn₃Sn, Fe₃Sn, Fe₆Sn, Fe₁₂Sn, Ni₃Sn, Ni₆Sn, Cu₃Sn, Cu₄Sn or Ti₃Sn.

(e) Phase A is composed of one or more of SrSi₂, BaSi₂, YSi₂, LaSi₂, TiSi₂, ZrSi₂, VSi₂, CrSi₂, MoSi₂, WSi₂, MnSi₂, CoSi₂, CuSi₂, FeSi₂ or NiSi₂, and Phase B is composed of one or more of TiSi, Ti₅Si₃, ZrSi, V₃Si, CrSi, Cr₂Si, Mo₃Si, W₃Si₂, MnSi, Mn₅Si₃, Mn₃Si, FeSi, Fe₅Si₃, Fe₃Si, CoSi, Co₂Si, Co₃Si, NiSi, Ni₃Si₂, Ni₂Si, CuSi, Cu₆Si₅, Cu₃Si or Cu₄Si.

(f) Phase A is composed of one or more of BaSi, TiSi, ZrSi, CrSi, MnSi, FeSi, CoSi, NiSi or CuSi, and Phase B is composed of one or more of Ti₅Si₃, V₃Si, Cr₂Si, Mo₃Si, W₃Si₂, Mn₅Si₃, Mn₃Si, Fe₅Si₃, Fe₃Si, Co₂Si, Co₃Si, Ni₃Si₂, Ni₂Si, Cu₆Si₅, Cu₃Si or Cu₄Si.

(g) Phase A is composed of one or more of Ti₅Si₃₁ W₃Si₂, Mn₅Si₃, Fe₅Si₃ or Cu₆Si₅, and Phase B is composed of one or more of V₃Si, Cr₂Si, Mo₃Si, Mn₃Si, Fe₃Si, Co₂Si, Co₃Si, Ni₂Si, Cu₃Si or Cu₄Si.

(h) Phase A is composed of one or more of SrSi, Cr₂Si, Co₂Si or Cu₄Si, and Phase B is composed of one or more of V₃Si, Mo₃Si, Mn₃Si, Fe₃Si, Co₃Si, Cu₃Si or Cu₄Si.

(i) Phase A is composed of one or more of SrAl₄, BaAl₄, BaAl₂, LaAl₄, LaAl₂, TiAl₃, ZrAl₃, ZrAl₂, VAl₃, V₅Al₈, CrAl₄, MoAl₃, WAl₄, MnAl₄, MnAl₃, Co₂Al₅, CuAl₂, FeAl₃, FeAl₂, NiAl₃ or Ni₂Al₃, and Phase B is composed of one or more of SrAl, BaAl, LaAl, La₃Al₂, TiAl, ZrAl, Zr₂Al, MO₃Al, MnAl, FeAl, Fe₃Al, CoAl, NiAl, CuAl or Cu₄Al₃.

(j) Phase A is composed of one or more of SrAl, BaAl, LaAl, TiAl, ZrAl, MnAl, FeAl, CoAl, NiAl or CuAl, and Phase B is composed of one or more of La₃Al₂, Zr₂Al, Mo₃Al, Fe₃Al or Cu₄Al₃.

The alloy particle of the present invention is preferably composed of 20 to 80 atomic % of Phase A, 80 to 20 atomic % of Phase B and 0 to 50 atomic % of other phases. As the third phase, there is for example a single phase composed only of one element selected from the element group m² (hereinafter referred to Phase C). Phase C causes no problem in battery performance provided that the amount thereof is not more than 10 atomic % in the alloy. The proportion of Phase C is more desirably 5 atomic % or less. Other phases comprising an element selected from the element group m¹ may be present.

It is preferable that any one of Phase A and Phase B is dispersed in the form of islands in the matrix of other phase or both of Phase A and Phase B are constituted of fine crystal grains. When the crystal grain is in the form of a needle, the above-mentioned suppressing of pulverization works more successfully. In this case, the crystal grain size is desirably 10 μm or less. The more preferable crystal grain size is 0.05 μm or more and 5 μm or less. When the crystal grain size is over 10 μm, the crystal grain itself collapses due to expansion stress in absorbing lithium, possibly causing pulverization. When the crystal grain is in the form of a needle, the aspect ratio is desirably 1.5 or more. When the crystal grain is in such a form, the difference of expansion stresses of Phase A and Phase B further decreases, and the effect for suppressing pulverization of the alloy particle increases.

It is preferable that the cross section of a crystal grain in Phase A and Phase B is 10⁻⁷ cm² or less. More preferably the cross section is 10⁻⁹ cm² or more and 10⁻⁸ cm² or less. The reason for this is that when the cross section of a crystal grain in Phase A and Phase B is over 10⁻⁷ cm², the crystal grain itself collapses due to expansion stress in absorbing lithium, and a possibility of pulverization increases.

It is more preferable that the above-mentioned negative electrode has a structure in which all or a part of Phase B is covered with Phase A. Owing to this structure, expansion stress of the alloy particle is suppressed more easily.

In a further preferable mode of the present invention, the alloy contains a phase having a composition represented by M⁷. By this phase, the effect for suppressing pulverization increases. M⁷ is a single element or a compound made of two or more elements selected from the above-mentioned element group m¹, and the content thereof is preferably from 10 to 50 atomic %, more preferably from 10 to 25 atomic % based on the total amount of whole particles. The elements in the element group m¹ are elements which do not easily react with lithium electrochemically, and due to the presence of them in the alloy, pulverization of the alloy particle due to expansion and contraction can be suppressed. The phase having a composition represented by M⁷ is desirably constituted of a plurality of crystal grains. Further, the crystal grain size may advantageously be 10 μm or less, more preferably 0.05 μm or more and 5 μm or less. When the crystal grain size is over 10 μm, phases not involved in charge and discharge are present in significant amounts, leading to a negative electrode having a lower capacity. An alloy preferably has a structure in which all or a part of the surface of the phase having a composition represented by M⁷ is coated with Phase A or Phase B. With this structure, expansion stress of the alloy particle is suppressed more easily.

If the compositions when Phase A and Phase B absorb maximum amounts of lithium are represented by Li_(y)M³ _(c)M⁴ and Li_(z)M⁵ _(d)M⁶ respectively, proportions thereof in respective alloys are represented by w¹ and w² in terms of atomic ratios and respective proportions of absorbed lithium are represented by L¹=y/(c+1) an L²=z/(d+1) in terms of atomic ratios, then it is preferable that the average value of L¹×w¹ and L²×w²; namely LW={(L¹×w¹)+(L²×w²)}/2 is 2 or less.

When the above-mentioned formulae are satisfied, expansion stresses of Phase A and Phase B are the smallest, and pulverization of an alloy particle is suppressed. When LW is over 2, expansion and contraction are not easily relaxed even if three phases, Phase A, Phase B and a phase having a composition represented by M⁷ are present. When cycle life characteristics are more important even if the capacity of the battery decreases slightly, LW is preferably 1 or less.

In another preferable mode of the present invention, a negative electrode is constituted of an alloy particle in which at least 50% or more of the surface of the particle containing at least one phase having a composition represented by the formula M⁸ _(e)M⁹ is covered with a phase having a composition represented by the formula M¹⁰ _(f)M¹¹ _(g). In the above-mentioned formulae, 0≦e≦5 and, g=1 and e≦f or g=0, each of M⁸ and M¹⁰ represents at least one element selected from the element group m¹, each of M⁹ and M¹¹ represents at least one element selected from the element group m², M⁸ and M⁹ represent different elements each other, and, M¹⁰ and M¹¹ represent different elements each other. Formation of a surface phase represented by the formula M¹⁰ _(f)M¹¹ _(g) suppresses cracking on the surface of an alloy particle, thereby to suppress pulverization of the particle. When the surface phase of an alloy particle has lower activity with lithium than that of an inner phase, there is also an action to prevent formation of an organic film on the surface of the particle by direct reaction with an organic solvent in an electrolyte. By this, charge and discharge efficiency increases, enabling long cycle life.

Covering of 50% or more of the whole surface of an alloy particle with the above-described surface phase allows the above-mentioned action to show an effect. When the covering ratio is less than 50%, many active planes of the particle are brought to the surface of the particle, thereby to lower the above-described action and effect.

In an alloy particle wherein the concentration of at least one element selected from the element group m¹ decreases in gradient from the surface of the particle toward the inner portion, the effect for suppressing pulverization increases further since a continuous inclination from phases having lower activity with lithium to phases having higher activity with lithium is formed.

The inner phase, a phase having a composition represented by M⁸ _(e)M⁹ gives excellent battery performances when a crystallite contained in the phase is as minute as possible. More specifically, the crystal grain size is advantageously not over 10 μm, and more preferably 0.01 μm or more and 1 μm or less. When the crystal grain size is smaller, grain boundary region between crystals increases, and lithium ions tend to move easily through the region. As a result, the reaction becomes uniform, and stable battery performances are obtained without a large load on a part of an alloy particle.

Also in the surface phase, a phase having a composition represented by M¹⁰ _(f)M¹¹ _(g), it is preferable that a crystallite contained in the phase is as minute as possible. More specifically, the crystal grain size is advantageously not over 10 μm, and more preferably 0.01 μm or more and 1 μm or less. Like the inner phase, when the crystal grain size is smaller, grain boundary region between crystals increases, and lithium ions tend to move easily through the region, and sufficient reaction throughout the inner phase becomes possible.

One preferable method for producing an alloy particle of the present invention is a gas atomizing method shown in the following example. However, a liquid quenching method, ion beam sputtering method, vacuum vapor deposition method, plating method, gas phase chemical reaction method, mechanical alloying method and the like can also be applied. The preferable method for producing a surface phase on an alloy particle includes a mechanical milling method and electroless plating method shown in the following examples. In addition, a mechanochemical method, CVD method, plasma method and the like can be applied.

When the diameter of an alloy particle used in a negative electrode of the present invention is over 45 μm, unevenness on the surface of the negative electrode increases, causing negative effects on battery performances since the thickness of a practical negative electrode sheet is about 80 μm. Particularly preferable particle size is 30 μm or less.

The negative electrode of the present invention preferably contains an electrically conductive agent in an amount of 1 to 50% by weight. More preferably, the amount is from 5 to 25% by weight. The electrically conductive agent is desirably a carbon material. The particularly desirable material is a graphite-based material.

The following examples further illustrate the present invention in detail. The present invention is not limited to such examples.

EXAMPLE 1

In this example, electrode characteristics of various alloys as negative electrode active material were evaluated. Alloys used in this example were synthesized by the following method.

First, various elements in the form of a block, plate or particle were mixed in a given ratio, before casting in an arc melting furnace. The resultant cast article was subjected to a gas atomizing method under an argon gas atmosphere to obtain an alloy particle. The diameter of a spray nozzle herein used is 1 mmφ, and the argon gas injection pressure was 100 kgf /cm². The resultant alloy particle was passed through a 45 μm mesh sieve to obtain particles having an average particle size of 28 μm.

The above-described particles were subjected to X-ray diffraction analysis to recognize a plurality of phases in each particle. This plurality of phases were classified into the above-mentioned Phase A, Phase B, Phase C and other phases which are shown in Table 1.

The above-described particles were also subjected to surface analysis by EPMA analysis to find that any alloy has a maximum crystallite size of 8 μm and an average crystallite size of 2.3 μm. The crystallite area of a phase satisfying the above-mentioned formula (2) or (3) is 5×10⁻⁸ cm² at maximum. In some of the above-mentioned alloy particles, phases composed solely of an element selected from the above-mentioned element group m² were observed. The composition ratio of such phases in the alloy was 5 atomic % or less based on the total amount. Content ratios are listed in Table 1.

To 7.5 g of each alloy particle, 2 g of a graphite powder is mixed as an electrically conductive agent, and 0.5 g of a polyethylene powder is mixed as a binder. 0.1 g of the mixture was molded under pressure into a disk having a diameter of 17.5 mm. For investigating characteristics of the electrode thus produced, a test cell shown in FIG. 1 was fabricated. In FIG. 1, numeral 1 designates a test electrode made of a molded mixture containing each alloy particle. This test electrode 1 is placed at the center of a case 2. A separator 3 made of a micro-porous polypropylene film is placed on the electrode 1, and an electrolyte solution was poured, then, the opening of the case 2 was closed with a sealing plate 6 having an inner surface adhered with a metallic lithium disk of 17.5 mm in diameter and a periphery portion equipped with a polypropylene gasket 5. The test cell is thus constituted. The electrolyte solution herein used was prepared by dissolving 1 mol/liter of lithium perchlorate (LiClO₄) into a mixed solvent of ethylene carbonate with dimethoxymethane at a volume ratio of 1:1.

In this test cell, the electrode was subjected to cathode polarization (corresponding to charging when the test electrode is regarded as the negative electrode) at a constant current of 0.5 mA until the electrode potential became 0 V vs. the lithium counter electrode, then, the electrode was subjected to anode polarization (corresponding to discharging) until the electrode potential became 1.5 V. These cathode polarization and anode polarization were repeated.

Initial discharge capacities of 1 g of respective alloys are compared in Table 1. The cathode polarization and anode polarization were repeated 10 cycles, then, the test electrode was removed from the cell and observed, to find no deposition of metallic lithium on the surface of the electrode made of any alloy. From these results, no generation of dendrites was recognized in the alloy active material for a negative electrode in the present example. Moreover, the test electrode after the cathode polarization was subjected to ICP analysis, to find that x in the formula (1) relating to the amount of lithium contained in the alloy did not exceed 10.

Then, for evaluation of the cycle life characteristics of a battery made by using the above-mentioned alloy as the negative electrode, a cylindrical battery as shown in FIG. 2 was produced in accordance with the following procedure.

A positive electrode active material LiMn_(1.8)Co_(0.2)O₄ was synthesized by mixing Li₂CO₃, Mn₃O₄ and CoCO₃ at a given molar ratio and heating the mixture at 900° C. The resultant was classified to obtain a positive electrode active material of 100 mesh or less.

To 100 g of the positive electrode active material, 10 g of a carbon powder as an electrically conductive agent and an aqueous dispersion of polytetrafluoroethylene as a binder (resin content: 8 g) were added to prepare a paste which was applied on a titanium core member, and subsequently dried and rolled to obtain a positive electrode plate.

A negative electrode was produced by mixing each alloy particle, a graphite powder as an electrically conductive agent, and polytetrafluoroethylene as a binder at a ratio by weight of 70:20:10, rendering the mixture into a paste using a petroleum-based solvent, applying the paste on a copper core member, then, drying this at 100° C. A porous polypropylene film was used as a separator.

A positive electrode plate 11 on which a positive electrode lead 14 made of the same material as that of the core member was fixed by spot welding, a negative electrode plate 12 on which a negative electrode lead 15 likewise made of the same material as that of the core member was fixed by spot welding, and a band-like separator 13 having larger width than both electrodes inserted between both electrodes, were spirally rolled up to form an electrode group. This electrode group was inserted into a battery case 18 while placing polypropylene insulating plates 16 and 17 to the top and the bottom thereof, a step portion was formed on the upper part of the case 18, then, the same electrolyte solution as described above was poured into the case, and the case was sealed with a sealing plate 19 having a positive electrode terminal 20.

The battery constituted as described above was subjected to a charge and discharge cycle test at a temperature of 30° C., at a charge and discharge current of 1 mA/cm², and a charge and discharge voltage in the range from 4.3 V to 2.6 V, and discharge capacities at 2nd cycle and the capacity maintenance rates at 100th cycle against the discharge capacity at 1st cycle were measured. The results are shown in table 1.

TABLE 1 Initial discharge Capacity Alloy Phase C capacity maintenance rate No. composition Phase A Phase B (at %) Other phase (mAh/g) (%) 1 CoSn CoSn₂ CoSn — — 770 75 2 CoSn₂ CoSn₂ CoSn Sn(5) — 860 69 3 MnSn MnSn₂ Mn₂Sn — — 690 81 4 Mn₂Sn MnSn₂ Mn₂Sn,Mn₃Sn — — 590 94 5 Mn₂Sn₃ MnSn₂ Mn₂Sn Sn(8) — 780 77 6 ZrSn ZrSn₂ Zr₄Sn — — 700 80 7 LaNi₂Sn LaSn₂ Ni₃Sn₂,Ni₃Sn — — 450 96 8 NiSn Ni₃Sn₄ Ni₃Sn Sn(2) — 520 94 9 NiCoSn NiCoSn Ni₃Sn Sn(2) — 550 94 10 Fe₅Sn₂ FeSn Fe₃Sn Sn(2) — 480 95 11 FeMnSn₂ FeSn₂ Fe₂Sn,Mn₃Sn — — 520 87 12 Ti₃Sn₂ Ti₆Sn₅ Ti₂Sn,Ti₃Sn — — 640 89 13 TiSn Ti₆Sn₅ Ti₂Sn Sn(5) — 850 81 14 Cu₃Sn₂ Cu₆Sn₅ Cu₃Sn — — 670 95 15 CuSn Cu₆Sn₅ Cu₃Sn Sn(6) — 720 86 16 FeCuSn Cu₆Sn₅ Cu₃Sn,Fe₆Sn — — 650 82 17 Fe₂CuSn Cu₆Sn₅ Cu₃Sn,Fe₁₂Sn — — 580 87 18 Fe₃CuSn Cu₆Sn₅ Cu₃Sn — Fe₁₈Sn 520 93 19 TiFeSn Ti₆Sn₅ Ti₃Sn,Fe₆Sn — — 600 91 20 Ti₂Sn Ti₂Sn Ti₃Sn — — 630 96 21 Ti_(1.8)Sn Ti₂Sn Ti₃Sn Sn(4) — 690 94 22 CoMnSn CoSn Mn₃Sn Sn(3) — 570 89 23 VCu₂Sn V₂Sn Cu₄Sn — — 530 91 24 VSi VSi₂ V₂Si — — 740 84 25 TiSi TiSi₂ TiSi,Ti₅Si₃ — — 710 90 26 Zr_(0.8)Si ZrSi₂ ZrSi Si(4) — 700 85 27 V₃Si₂ VSi₂ V₃Si — — 640 89 28 MnSi MnSi₂ MnSi,Mn₃Si — — 660 87 29 Fe₃Si₂ FeSi₂ FeSi,Fe₃Si Si(2) — 630 92 30 CoSi CoSi₂ CoSi,Co₂Si Si(2) — 650 88 31 Co₃Si₂ CoSi₂ CoSi,Co₂Si,Co₃Si — — 570 93 32 NiSi NiSi₂ NiSi Si(4) — 730 78 33 Ni₂Si NiSi₂ NiSi,Ni₃Si₂ — — 510 89 34 Ti₂BaSi₂ BaSi,TiSi Ti₅Si₃ — — 580 87 35 Ti₂Si TiSi Ti₅Si₃ Si(4) — 620 84 36 Co₂Si CoSi Co₂Si Si(1) — 600 89 37 Fe₂Si FeSi Fe₅Si₃ — — 490 92 38 FeMoSi FeSi Mo₃Si Si(2) — 510 89 39 Mn₂Si MnSi Mn₅Si₃,Mn₂Si — — 480 93 40 Mn₃Si Mn₅Si₃ Mn₃Si — — 440 96 41 Co₃Si Co₂Si Co₃Si Si(3) — 520 93 42 NiCoAl₃ NiAl₄,CoAl₂ CoAl — — 770 75 43 CoAl₂ CoAl₂ CoAl,Co₃Al₂ — — 680 77 44 CuAl₂ CuAl₂ CuAl,Cu₄Al₃ — — 720 75 45 FeAl₂ FeAl₃ FeAl — — 780 72 46 TiAl₃ TiAl₃ TiAl Al(5) — 750 78 47 MnAl₃ MnAl₄ MnAl — — 700 74 48 LaAl₂ LaAl La₃Al₂ — — 620 83 49 FeAl FeAl Fe₃Al Al(4) — 630 84 50 CuAl CuAl Cu₄Al₃ Al(3) — 650 81

For comparison, batteries were produced by using a particle composed of a Sn single substance and an Al single substance (average particle size: 26 μm, average crystallite size: 15 μm), a particle composed only of a Cu₆Sn₅ phase, a particle composed only of a FeAl phase (in each case, average particle size is 28 μm, an average crystallite size is 2.1 μm), a particle composed of Mg₂Ge phase-Mg phase (average particle size: 25 μm, average crystallite size: 3.2 μm, Mg₂Ge/Mg=7/3 (by atom)), a particle composed of Mg₂Sn phase-Mg phase (average particle size: 27 μm, average crystallite size: 5.3 μm, Mg₂Sn/Mg=8/2 (by atom)) and a particle composed of Mg₂Sn phase-Sn phase (average particle size: 27 μm, average crystallite size: 5.3 μm, Mg₂Sn/Sn=7/3 (by atom)), and discharge capacities at 2nd cycle and the capacity maintenance rates at 100th cycle against the discharge capacity at 1st cycle of the battery were measured and are shown in table 2.

TABLE 2 Initial discharge Capacity Alloy Phase C capacity maintenance rate composition Phase A Phase B (at %) Other phase (mAh/g) (%) Sn — — Sn(100) — 620 12 Al — — Al(100) — 730  5 Cu₆Sn₅ Cu₆Sn₅ — — — 550 34 FeAl FeAl — — — 600 29 Mg₂Ge—Mg Mg₂Ge — — Mg 530 22 Mg₂Sn—Mg Mg₂Sn — — Mg 490 33 Mg₂Sn—Sn Mg₂Sn — Sn(30) — 650 20

Batteries produced by using alloy active materials of the present invention as the negative electrode showed remarkably high capacity and improved cycle life characteristics as compared with comparative examples.

EXAMPLE 2

Powders or blocks of elements constituting a negative electrode alloy material were placed in a melting bath at given charging ratio, then, melted by heating, the melted substance was quenched by a roll quenching method for solidification. The obtained solidified substance was ground by a ball mill, and classified by a sieve to obtain alloy particles having a particle size of 45 μm or less.

It was confirmed that these alloys are constituted of at least three phases by electron microscope observation, element analysis and X-ray structure analysis. It was also found that phases were present in ratios as shown in Table 3.

The above-mentioned alloys were also subjected to surface analysis in accordance with EPMA analysis, to find that any alloy had a maximum crystallite size of 7 μm and an average crystallite size of 2.0 μm. The phase satisfying the above-mentioned formulae (2), (3) and (4) had a maximum crystallite area of 3×10⁻⁸ cm². In some alloy particles, a phase is observed composed only of an element selected from the above-mentioned element group m², and the composition ratio of these phases was 5 atomic % or less based on the total amount.

The electrode characteristics as the negative electrode active material were evaluated by a test cell as shown in FIG. 1 in the same manner as in Example 1. The initial discharge capacities per 1 g of each alloy are shown in Table 3. The cathode polarization and the anode polarization were repeated for 10 cycles, then, the test cell was disassembled, the test electrodes were removed and observed, to find no deposition of metallic lithium on the surface of the electrode made of any alloy. From these results, no generation of dendrites was recognized in the alloy active material for a negative electrode in the present example. Furthermore, the test electrode after the cathode polarization was subjected to ICP analysis, to find that x in the formula (1) relating to the amount of lithium contained in the alloy did not exceed 10.

Cylindrical batteries using the above-mentioned alloys as the negative electrode were produced in the same manner as in Example 1, and the cycle life characteristics were evaluated under the same conditions. The results are shown in Table 3.

Batteries produced by using active materials of the present invention as the negative electrode showed remarkably high capacity and improved cycle life characteristics as compared with comparative examples shown in Table 2.

TABLE 3 Initial discharge Capacity Alloy Phase C capacity maintenance rate No. composition Phase A Phase B (at %) Other phase (mAh/g) (%) 51 Fe₂Sn FeSn₂ FeSn,Fe₃Sn — Fe 610 94 52 Co₂Sn CoSn₂ CoSn — Co 630 91 53 Mn_(2.5)Sn MnSn₂ Mn₂Sn,Mn₃Sn — Mn 550 97 54 FeMnSn₂ FeSn₂,MnSn₂ FeSn,Mn₂Sn — Fe 740 81 55 NiFeSn₂ NiSn₂ FeSn — Fe 630 79 56 CoCu₃Sn CoSn₂ Cu₃Sn — Cu 440 97 57 Mn₂FeSn₂ Mn₂Sn Fe₃Sn — Mn 710 89 58 NiSi NiSi₂ Ni₅Si₃ — Ni 580 91 59 Mo₃Si₂ MoSi₂ Mo₃Si — Mo 620 88 60 W₂Si WSi₂ W₃Si₂ — W 520 94 61 FeSi FeSi₂ FeSi,Fe₅Si₃ Si(1) Fe 590 94 62 CuSi CuSi₂ Cu₆Si₅ — Cu 660 85 63 VFeSi VSi Fe₅Si₃ — V 460 91

EXAMPLE 3

In this example, electrode characteristics as the negative electrode active material of alloys having a surface coating phase were evaluated.

Alloy active materials selected from Cu (particle), Co (particle), Mn (block), Ni (particle), Ti (block), Sn (particle), Si (particle) and Al (powder) were mixed at given combination and molar ratio, and the mixture was cast in an arc melting furnace. The resultant cast article was processed by a gas atomizing method to obtain spherical particles. These alloy particles were passed through a 45 μm sieve to obtain particles having an average particle size of 28 μm.

The above-mentioned particles were subjected to X-ray diffraction analysis, to find that any of the particle had a plurality of alloy phases or single phase, and a phase having a composition satisfying the above-mentioned formula (8) was present without fail. Further, the above-mentioned particles were subjected to EPMA analysis, to find that in any particle, the crystal grain size of a phase satisfying the above-mentioned formula (8) was 5 μm at maximum, and the average crystal grain size was 1.3 μm.

Production of the surface phase on the above-mentioned alloy particle was conduced in accordance with a method in which a Ni powder having an average particle size of 0.03 μm, Cu powder having an average particle size of 0.05 μm, Ti powder having an average particle size of 0.05 μm, or Mn powder having an average particle size of 0.1 μm was mixed, and a method in which Ni, Co or Cu was applied on the surface using a commercially available Ni electroless plating solution, Co electroless plating solution, or Cu electroless plating solution.

In the method of mixing a powder, the above-mentioned alloyl powder and the above-mentioned metal powder were mixed at a ratio of 10:1 (by weight), then, the mixture was allowed to roll by a planetary ball mill for 10 minutes to make the metal powder to deposit on the surface of the alloy particle.

In the plating method, above-mentioned alloy particles were placed in respective electroless plating bathes, and stirred at 50° C. for Ni, 70° C. for Co and 20° C. for Cu to accomplish plating for 30 minutes.

Particles carrying the above-mentioned surface phases produced were subjected to given heat treatment, to cause diffusion from the surface phase to the inner phase of a metallic element constituting the surface layer, forming an inclination in concentration so that the concentration of the metallic element decreases from the surface to the inner portion. In this procedure, the heat treatment was conducted under argon atmosphere, and heating up to given treating temperature was conducted in 3 hours, and this treating temperature was kept for 12 hours. The particles were left for cooling.

As a result, a surface phase as shown in Table 4 was obtained (in this table, a phase present on the outermost surface of a particle in largest amount is shown.). SEM photographs of sections of various particle were observed, to confirm that in all particles, the surface phase was present at a coating ratio of at least 50%.

The electrode characteristics as the negative active material of these alloy particles were evaluated in the test cell as shown in FIG. 1 in the same manner as in Example 1. The initial discharge capacities per 1 g of these active materials are shown in Table 4. Regarding all active materials, a test cell subjected to the cathode polarization and another test cell subjected to the cathode polarization and the anode polarization repeated for 10 cycles were disassembled and the test electrodes were removed and observed. The result was that there was no deposition of metallic lithium on the surface of the electrodes. From these results, no generation of dendrites was recognized in the negative electrode active material in the present example. Further, the test electrode after the cathode polarization was subjected to ICP analysis, to find that x in the formula (1) relating to the amount of lithium contained in the alloy did not exceed 10.

Then, for evaluation of the cycle life characteristics of a battery made by using the above-mentioned alloy as the negative electrode, a cylindrical battery as shown in FIG. 2 was produced in accordance with the same method as in Example 1.

These batteries were subjected to a charge and discharge cycle test at a temperature of 30° C., at a charge and discharge current of 1 mA/cm², and a charge and discharge voltage in the range from 4.3 V to 2.6 V. Discharge capacities at 2nd cycle and capacity maintenance rates at 200th cycle against the discharge capacity at 1st cycle are shown in table 4.

TABLE 4 Initial discharge Capacity Alloy Surface Heat capacity maintenance rate particle Inner phase treatment treatment Surface phase (mAh/g) (%) NiSi₂ NiSi₂,Si — — NiSi₂ 720 68 Ni(plating) — Ni 690 91 900° C. NiSi 680 95 Ni(powder) — Ni 690 93 900° C. Ni₂Si 690 97 Cu₆Sn₅ Sn,Cu₆Sn₅ — — Cu₆Sn₅ 580 75 Cu(powder) — Cu 550 89 400° C. Cu₃Sn 560 93 Cu(plating) — Cu 570 95 400° C. Cu₃Sn 580 98 Ni(powder) — Ni 550 93 700° C. Cu₂NiSn 590 99 CoSn₂ Sn,CoSn₂,CoSn — — CoSn₂ 770 82 Co(plating) — Co 740 95 950° C. Co₃Sn₂ 750 97 Ti₂Sn Ti₂Sn — — Ti₂Sn 560 80 Ti(powder) — Ti 540 97 1000° C. Ti₅Sn 540 99 MnAl MnAl₄,MnAl,Mn — — MnAl 490 77 Mn(powder) — Mn 450 93 600° C. Mn₃Al 470 97

For comparison, discharge capacities at 2nd cycle and the capacity maintenance rates at 200th cycle against the discharge capacity at 1st cycle of batteries using alloy particles forming no surface phase formed are shown in table 4.

It is found that batteries produced by using active materials having surface phases show remarkably improved cycle life characteristics as compared with batteries using active materials having no surface phase as the negative electrode.

In the above-mentioned examples, the cylindrical batteries are explained, however, the form of the battery of the present invention is not limited to cylindrical, and secondary batteries in other forms such as a coin type, rectangular type, flat type and the like can be applied likewise. In the above examples, LiMn_(1.8)Co_(0.2)O₄ was used as the positive electrode active material, however, it is not to mention that active materials having reversibility for charging and discharging typically including LiMn₂O₄, LiCoO₂, LiNiO₂ and the like can be used.

INDUSTRIAL APPLICABILITY

As described above, in accordance with the present invention, non-aqueous electrolyte secondary batteries affording high energy density with high capacity and extremely excellent cycle life characteristics can be obtained. 

What is claimed is:
 1. A non-aqueous electrolyte secondary battery comprising a rechargeable positive electrode, a rechargeable negative electrode and a non-aqueous electrolyte, wherein said negative electrode comprises alloy particles having a composition represented by the formula: Li_(x)M¹ _(a)M²  (1) wherein M¹ represents at least one element selected from the element group m¹ consisting of Ti, Zr, V, Sr, Ba, Y, La, Cr, Mo, W, Mn, Co, Ir, Ni, Cu and Fe, M² represents at least one element selected from the element group m² consisting of Mg, Ca, Al, In, Si, Sn, Pb, Sb and Bi, M¹ and M² represent different elements from each other, and wherein 0≦x≦10, 0.1≦a≦10, with the proviso that 2≦a≦10 when M¹ is composed only of Fe, and having at least two phases which are different in composition from each other.
 2. The non-aqueous electrolyte secondary battery in accordance with claim 1, wherein said at least two phases have compositions represented by the formula (2) and the formula (3), respectively: M³ _(c)M⁴  (2) M⁵ _(d)M⁶  (3) wherein each of M³ and M⁵ represents at least one element selected from said element group m¹, each of M⁴ and M⁶ represents at least one element selected from said element group m², and wherein 0.25≦c<3, 1≦d≦10 and c<d.
 3. The non-aqueous electrolyte secondary battery in accordance with claim 2, wherein a part or all of a phase having a composition represented by the formula (3) is covered with a phase having a composition represented by the formula (2) in said alloy.
 4. The non-aqueous electrolyte secondary battery in accordance with claim 3, wherein said alloy further has a phase having a composition represented by the formula (4): M⁷  (4) wherein M⁷ represents a single element or a compound made of two or more elements selected from said element group m¹ and the proportion of this phase is from 10 to 50 atomic % based on the total amount of whole particles.
 5. The non-aqueous electrolyte secondary battery in accordance with claim 4, wherein all or a part of the surface of a phase having a composition represented by said formula (4) is covered with a phase having a composition represented by the formula (2) or the formula (3).
 6. The non-aqueous electrolyte secondary battery in accordance with claim 2, wherein when phases having compositions represented by said formula (2) and (3) absorb maximum amounts of lithium, if the compositions are represented by Li_(y)M³ _(c)M⁴ and Li_(z)M⁵ _(d)M⁶ respectively, proportions thereof in respective alloys are represented by w¹ and w² in terms of atomic ratios and respective proportions of absorbed lithium are represented by L¹=y/(c+1) an L²=z/(d+1) in terms of atomic ratios, then {(L¹×w¹)+(L²×w²)}/2 is 2 or less.
 7. The non-aqueous electrolyte secondary battery in accordance with claim 1, wherein said negative electrode is composed of alloy particles in which at least 50% or more of the surface of the particle containing at least one phase having a composition represented by the formula M⁸ _(e)M⁹ is covered with a phase having a composition represented by the formula M¹⁰ _(f)M¹¹ _(g), and wherein in said formulae, 0≦e≦5 and, g=1 and e≦f or g=0, each of M⁸ and M¹⁰ represents at least one element selected from said element group m¹, each of M⁹ and M¹¹ represents at least one element selected from said element group m², M⁸ represents a different element from M⁹ and M¹⁰ represents a different element from M¹¹.
 8. The non-aqueous electrolyte secondary battery in accordance with claim 7, wherein the concentration of at least one element selected from said element group m¹ in said alloy particle decreases in gradient from the surface of the particle toward the inner portion.
 9. The non-aqueous electrolyte secondary battery in accordance with claim 1, wherein the average size of the alloy particles constituting said negative electrode is 45 μm or less.
 10. The non-aqueous electrolyte secondary battery in accordance with claim 1, wherein said negative electrode contains an electrically conductive agent in an amount of 1% by weight or more and 50% by weight or less.
 11. A non-aqueous electrolyte secondary battery comprising a rechargeable positive electrode, a rechargeable negative electrode and a non-aqueous electrolyte, wherein said negative electrode comprises alloy particles having a composition represented by the formula: Li_(x)M¹ _(a)M²  (1) wherein M¹ represents at least one element selected from the element group m¹ consisting of Ti, Zr, V, Sr, Ba, Y, La, Cr, Mo, W, Mn, Co, Ir, Ni, and Cu, M² represents at least one element selected from the element group m² consisting of Mg, Ca, Al, In, Si, Sn, Pb, Sb and Bi, M¹ and M² represent different elements from each other, and wherein 0≦x≦10 and 0.1≦a≦10, and having at least two phases which are different in composition from each other.
 12. A non-aqueous electrolyte secondary battery comprising a rechargeable positive electrode, a rechargeable negative electrode and a non-aqueous electrolyte, wherein said negative electrode comprises alloy particles having a composition represented by the formula: Li_(x)M¹ _(a)M²  (1) wherein M¹ represents at least one element selected from the element group m¹ consisting of Ti, Zr, V, Sr, Ba, Y, La, Cr, Mo, W, Mn, Co, Ir, Ni, Cu and Fe, M² represents at least one element selected from the element group m² consisting of Mg, Ca, Al, In, Sn, Pb, Sb and Bi, M¹ and M² represent different elements from each other, and wherein 0≦x≦10, 0.1≦a≦10, with the proviso that 2≦a≦10 when M¹ is composed only of Fe, and having at least two phases which are different in composition from each other. 